JP2008248307A - High toughness and high speed steel-base sintered alloy - Google Patents
High toughness and high speed steel-base sintered alloy Download PDFInfo
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本発明は、高速度鋼系焼結合金に関し、より具体的には、耐摩耗性及び靱性にすぐれる高速度鋼系焼結合金に関する。 The present invention relates to a high-speed steel-based sintered alloy, and more specifically to a high-speed steel-based sintered alloy having excellent wear resistance and toughness.
鋼材の熱間圧延又は冷間圧延用ロール、塑性加工用金型、プラスチック成形機のシリンダー、スクリュー等は、耐摩耗性、耐肌荒れ性が要求されると共に、耐事故性が要求される。これら用途の材料として、これまで、ＪＩＳに規定された合金工具鋼や高速度鋼が用いられていたが、近年では、高速度鋼系の合金組成を有する焼結合金が使用されている。 Rolls for hot rolling or cold rolling of steel materials, dies for plastic working, cylinders and screws of plastic molding machines are required to have wear resistance and rough skin resistance, as well as accident resistance. Up to now, alloy tool steels and high-speed steels defined in JIS have been used as materials for these applications, but recently, sintered alloys having a high-speed steel-based alloy composition have been used.
耐摩耗性にすぐれる高速度鋼系の合金組成を有する粉末合金として、Ｃ：１.５〜３.５％、 Ｓｉ：０.６％以下、Ｍｎ：０.６％以下、 Ｃｒ：０.５〜２５％、２Ｍｏ＋Ｗ：１.５〜４５％、 Ｎｉ：３.０％以下、Ｖ、Ｔｉ、Ｎｂ、Ｔａの内の１種以上を総計で０.５〜１２.０％、Ｎ：０.０５〜０.５％及び残部実質的にＦｅからなるものがある（特許文献１）。 As a powder alloy having a high-speed steel-based alloy composition with excellent wear resistance, C: 1.5 to 3.5%, Si: 0.6% or less, Mn: 0.6% or less, Cr: 0.00 5 to 25%, 2Mo + W: 1.5 to 45%, Ni: 3.0% or less, 0.5% to 12.0% in total of one or more of V, Ti, Nb and Ta, N: 0 There are some which consist of 0.05 to 0.5% and the balance substantially Fe (Patent Document 1).
この特許文献に示された合金は、所定の焼入れ及び焼戻しの調質熱処理を施すことにより、マルテンサイト又はベイナイト相の硬質基地に微細な炭化物粒子が分散した組織を有し、高い硬度(例えばＨＲＣ６５以上)が得られるため、すぐれた耐摩耗性を発揮することができる。しかし、硬度が高くなるほど靱性は低くなる傾向があるため、大きな応力がかかる苛酷な使用環境では靱性が不足し、耐事故性の点では必ずしも十分とは言えなかった。
使用環境の苛酷化により、耐摩耗性は多少低下しても、靱性にすぐれる合金が要請されている。
The alloy shown in this patent document has a structure in which fine carbide particles are dispersed in a hard matrix of martensite or bainite phase by performing a predetermined tempering and tempering heat treatment, and has a high hardness (for example, HRC65 Thus, excellent wear resistance can be exhibited. However, since the toughness tends to decrease as the hardness increases, the toughness is insufficient in a severe use environment where a large stress is applied, and it cannot be said that the accident resistance is sufficient.
There is a demand for an alloy having excellent toughness even if the wear resistance is somewhat lowered due to the severe use environment.
本発明の目的は、所定の硬度を具えて耐摩耗性を確保すると共に、すぐれた靱性によって耐事故性が良好な高速度鋼系焼結合金を提供することである。 An object of the present invention is to provide a high-speed steel-based sintered alloy having a predetermined hardness and ensuring wear resistance and having good accident resistance due to excellent toughness.
発明者らは、硬度と靱性が相反する性質であることに着目し、合金基地(マトリックス)中のＣ量、及びＣｒ、Ｍｏ、Ｗ、Ｖ、Ｔｉ、Ｎｂ、Ｔａからなる炭化物生成元素の量を制御することにより、熱処理時のオーステナイトからマルテンサイト変態量を、最低限の耐摩耗性を確保できる程度に、少なく抑えて合金の高硬度化を抑制することにより、所定の靱性を得られるようにした。 The inventors pay attention to the fact that hardness and toughness are contradictory properties, and the amount of C in the alloy matrix (matrix) and the amount of carbide generating elements composed of Cr, Mo, W, V, Ti, Nb, Ta. By controlling the amount of martensite transformation from austenite during heat treatment to a level that can ensure the minimum wear resistance, it is possible to obtain a predetermined toughness by suppressing the increase in hardness of the alloy I made it.
具体的には、本発明の高速度鋼系焼結合金は、重量％にて、Ｃ：０.５％以上、１.５％未満、Ｓｉ：０.６％以下、Ｍｎ：０.６％以下、Ｃｒ：０.５〜１０.０％、Ｍｏ：０.５〜１５％、Ｗ：０.５〜２０％、Ｖ、Ｔｉ、Ｎｂ及びＴａからなる群から選択される少なくとも一種を合計量で０.５〜２０％、残部Ｆｅ及び不可避的不純物からなり、Ｃbalが−１.５以上、−０.５以下の範囲、好ましくは−１.０以上、−０.５以下の範囲にあることを特徴とする。なお、Ｃbal＝Ｃ−Ｃsticとし、Ｃstic＝０.０６Ｃｒ＋０.０６３Ｍｏ＋０.０３３Ｗ＋０.２４Ｖ＋０.２５Ｔｉ＋０.１３Ｎｂ＋０.０６６Ｔａとしており、Ｃsticは、炭化物の形成に必要なＣの量を表し、Ｃbalはマトリックスに残るＣの量を表している。
本発明の焼結合金は、必要に応じて、Ｎｉ：０.５〜３％及び／又はＮ：０.１〜０.５％を含むことができるし、また、Ｃｏ：７〜２０％を含むこともできる。
Specifically, the high-speed steel-based sintered alloy of the present invention is C: 0.5% or more, less than 1.5%, Si: 0.6% or less, Mn: 0.6% by weight%. Hereinafter, the total amount of at least one selected from the group consisting of Cr: 0.5 to 10.0%, Mo: 0.5 to 15%, W: 0.5 to 20%, V, Ti, Nb and Ta 0.5 to 20%, balance Fe and inevitable impurities, and Cbal is in the range of -1.5 or more and -0.5 or less, preferably in the range of -1.0 or more and -0.5 or less. It is characterized by being. Incidentally, the C bal = C-C stic, C stic = 0.06Cr + 0.063Mo + 0.033W + 0.24V + 0.25Ti + 0.13Nb + 0.066Ta and to have, C stic represents the amount of C necessary for forming the carbide, C bal Represents the amount of C remaining in the matrix.
The sintered alloy of the present invention may contain Ni: 0.5 to 3% and / or N: 0.1 to 0.5% as required, and Co: 7 to 20%. It can also be included.
本発明の焼結合金は、約１１００〜１２００℃の温度で加熱した後強制空冷による焼入れを行ない、次に、約５００〜６００℃の温度での焼戻しを３回繰り返すことにより、硬度がＨＲＣ５０〜６２、シャルピー衝撃強さ３０×１０4Ｊ／ｍ2以上の特性を得ることができる。好ましくは、硬度がＨＲＣ５５〜６０、シャルピー衝撃強さ５０×１０4Ｊ／ｍ2以上である。 The sintered alloy of the present invention is hardened by forced air cooling after being heated at a temperature of about 1100 to 1200 ° C., and then tempering at a temperature of about 500 to 600 ° C. three times to obtain a hardness of HRC 50 to 62, characteristics with Charpy impact strength of 30 × 10 4 J / m 2 or more can be obtained. Preferably, the hardness is HRC 55-60, and Charpy impact strength is 50 × 10 4 J / m 2 or more.
本発明の焼結合金は、硬度がＨＲＣ５０〜６２(好ましくはＨＲＣ５５〜６０)であるから、所定の耐摩耗性を具備することができる。またこの硬度は、高速度鋼系合金としては低硬度であり、シャルピー衝撃強さ３０×１０4Ｊ／ｍ2以上(好ましくは５０×１０4Ｊ／ｍ2以上)の高靱性を得ることができるから、すぐれた耐事故性を発揮することができる。
従って、硬度と靱性の効果的な組合せが重要とされる、鋼材の熱間圧延又は冷間圧延用ロール、塑性加工用金型、プラスチック成形機のシリンダー、スクリュー等の材料として有用である。
なお、これら製品の外面側又は内面側のどちらか一方の部分に、より高い硬度(例えばＨＲＣ６３以上)及び耐摩耗性が所望されるときは、より高い硬度及び耐摩耗性を得ることができる合金(例えば、特許文献１の高速度鋼系合金)の第１層に、靱性にすぐれる本発明合金の第２層を一体化させた複合製品にすればよい。前記第１層と前記第２層は、製品の要求特性に応じて、第１層を外面側に、第２層を内面側に設けることができるし、その逆も可能である。
Since the sintered alloy of the present invention has a hardness of HRC 50 to 62 (preferably HRC 55 to 60), it can have predetermined wear resistance. Moreover, this hardness is low as a high-speed steel alloy, and high toughness with Charpy impact strength of 30 × 10 4 J / m 2 or more (preferably 50 × 10 4 J / m 2 or more) can be obtained. Because it can, it can demonstrate excellent accident resistance.
Therefore, it is useful as a material such as a roll for hot rolling or cold rolling of steel, a mold for plastic working, a cylinder of a plastic molding machine, a screw, etc., in which an effective combination of hardness and toughness is important.
In addition, when higher hardness (for example, HRC63 or more) and wear resistance are desired for either one of the outer surface side and the inner surface side of these products, an alloy capable of obtaining higher hardness and wear resistance. What is necessary is just to make it the composite product which integrated the 2nd layer of this invention alloy excellent in toughness with the 1st layer (for example, high speed steel type alloy of patent document 1). The first layer and the second layer can be provided on the outer surface side and the second layer on the inner surface side, or vice versa, depending on the required characteristics of the product.
本発明の高速度鋼系焼結合金は上記の組成を有し、合金マトリックスに残存するＣの量、つまりＣbalの値を、−１.５以上、−０.５以下の範囲に規定したことに特徴を有する。
各成分の範囲の限定理由及びＣbalの意義について、以下に説明する。
High speed steel based sintered alloy of the present invention has the above composition, the amount of C remaining in the alloy matrix, i.e. the value of C bal, -1.5 or more, as specified in the range of -0.5 or less It has a special feature.
The reason for limiting the range of each component and the significance of Cbal will be described below.
Ｃ：０.５％以上、１.５％未満
Ｃは、炭化物形成元素であり、Ｖ、Ｔｉ、Ｎｂ、Ｔａ、Ｗ、Ｍｏ、Ｃｒ等と結合して、ＭＣ型、Ｍ2Ｃ型、Ｍ6Ｃ型の硬質炭化物を形成し、合金の耐摩耗性を高める。このため、少なくとも０.５％以上含有させる。しかし、Ｃを多量に含有すると、靱性が悪化し、欠け割れが発生し易くなる。従って、上限を１.５％未満とする。
C: 0.5% or more and less than 1.5% C is a carbide forming element, which is combined with V, Ti, Nb, Ta, W, Mo, Cr, and the like to form MC type, M 2 C type, M 6 Forms C-type hard carbide to increase the wear resistance of the alloy. For this reason, it is made to contain at least 0.5% or more. However, when a large amount of C is contained, the toughness is deteriorated and cracking is likely to occur. Therefore, the upper limit is made less than 1.5%.
Ｓｉ：０.６％以下
Ｓｉは脱酸作用を有する。しかし、多量に含有すると材料を脆化させるため、上限は０.６％とする。
Si: 0.6% or less Si has a deoxidizing action. However, the upper limit is made 0.6% because the material becomes brittle if contained in large amounts.
Ｍｎ：０.６％以下
Ｍｎは脱酸作用を有する。しかし、多量に含有すると材料を脆化させるため、上限は０.６％とする。
Mn: 0.6% or less Mn has a deoxidizing action. However, the upper limit is made 0.6% because the material becomes brittle if contained in large amounts.
Ｃｒ：０.５〜１０.０％
Ｃｒは、Ｍ6Ｃ型の炭化物を生成し、耐摩耗性を向上させるので少なくとも０.５％以上含有させる。しかし、あまりに多く含有すると炭化物量が過多となるため、上限は１０.０％に規定する。好ましくは４〜７％である。
Cr: 0.5 to 10.0%
Cr produces M 6 C type carbide and improves wear resistance, so it is contained at least 0.5% or more. However, if the content is too large, the amount of carbide becomes excessive, so the upper limit is specified at 10.0%. Preferably it is 4 to 7%.
Ｍｏ：０.５〜１５％
Ｍｏは、Ｍ2Ｃ型炭化物を生成し、耐摩耗性を向上させるので少なくとも０.５％以上含有させる。しかし、あまりに多く含有すると炭化物量が過多となるため、上限は１５％に規定する。好ましくは１〜１０％であり、さらに好ましくは１.５〜５％である。
Mo: 0.5 to 15%
Mo generates M 2 C type carbide and improves wear resistance, so it is contained at least 0.5% or more. However, if the content is too large, the amount of carbide becomes excessive, so the upper limit is defined as 15%. Preferably it is 1 to 10%, and more preferably 1.5 to 5%.
Ｗ：０.５〜２０％
Ｗは、Ｍ2Ｃ型炭化物を生成し、耐摩耗性を向上させるので少なくとも０.５％以上含有させる。しかし、あまりに多く含有すると炭化物量が過多となるため、上限は２０％に規定する。好ましくは３〜６％である。
W: 0.5-20%
W forms M 2 C type carbide and improves wear resistance, so it is contained at least 0.5% or more. However, if the content is too large, the amount of carbide becomes excessive, so the upper limit is defined as 20%. Preferably it is 3 to 6%.
Ｖ、Ｔｉ、Ｎｂ、Ｔａのうちの少なくとも一種：合計量で０.５〜２０％
Ｖ、Ｔｉ、Ｎｂ、Ｔａは、ＭＣ型炭化物を生成し、耐摩耗性には、ＭＣ型炭化物が顕著な効果を奏するので、これら元素の少なくとも一種を合計量で０.５％以上含有させる。しかし、あまりに多く含有すると炭化物量が過多となるため、上限は合計量で２０％に規定する。好ましくは０.５〜６％である。
At least one of V, Ti, Nb, Ta: 0.5 to 20% in total
V, Ti, Nb, and Ta produce MC type carbides, and MC type carbides have a remarkable effect on wear resistance. Therefore, at least one of these elements is contained in a total amount of 0.5% or more. However, if the content is too large, the amount of carbide becomes excessive, so the upper limit is defined as 20% in total. Preferably it is 0.5 to 6%.
Ｃbal：−１.５以上、−０.５以下
前述したように、本発明の高速度鋼系焼結合金は、合金基地(マトリックス)中のＣ量を制御することにより、熱処理時のマルテンサイト変態量を抑制するものである。
Ｃは、一般的に、炭化物形成に１００％使用されるわけではなく、マトリックスに分散して残存する。マトリックスに残ったＣは、熱処理時にオーステナイトから硬質のマルテンサイトへの変態を促し、合金の高硬度化をすすめ、その一方で靱性を低下させる。
そこで、合金設計上のＣ量と、他の元素と炭化物を形成する理論上のＣ量(Ｃstic)との差から、マトリックスに残る理論上のＣ量(Ｃbal)を算出し、Ｃbalを−１.５以上、−０.５以下の範囲に規定した。Ｃbal値が−(マイナス)を示しているが、これは理論上の値であり、Ｃbalが計算上この範囲にあっても、実際の合金においてはマトリックス中にＣが残存する。
Ｃbalが−１.５より小さいとマルテンサイト化が少なくなり、合金に必要な硬度が得られない。一方、Ｃbalが−０.５より大きいとマルテンサイト化が進みすぎて硬度が高くなり、本発明の目的にあった靱性を得ることができない。
なお、Ｃsticは、炭化物形成元素の種類に応じて次式で与えられる。
Ｃstic＝０.０６Ｃｒ＋０.０６３Ｍｏ＋０.０３３Ｗ＋０.２４Ｖ＋０.２５Ｔｉ＋０.１３Ｎｂ＋０.０６６Ｔａ
本発明の高速度鋼系焼結合金は、Ｃbalが−１.５以上、−０.５以下の範囲となるように、Ｃ、Ｃｒ、Ｍｏ、Ｗ、Ｖ、Ｔｉ、Ｎｂ、Ｔａの量を調整することにより、熱処理での焼入れ性能を低下させるようにした。これにより、一般的な高速度鋼と同じ条件の熱処理を施しても、得られる硬度は比較的低い範囲(ＨＲＣ５０〜６２)であり、高い靱性を得ることができる。
C bal : -1.5 or more, -0.5 or less As described above, the high-speed steel-based sintered alloy of the present invention controls the amount of C in the alloy matrix (matrix), so It suppresses the amount of site transformation.
C is generally not used 100% for carbide formation but remains dispersed in the matrix. C remaining in the matrix promotes transformation from austenite to hard martensite during the heat treatment, and promotes higher hardness of the alloy while reducing toughness.
Therefore, the theoretical C amount (C bal ) remaining in the matrix is calculated from the difference between the C amount in the alloy design and the theoretical C amount (C stic ) that forms carbide with other elements, and C bal Was specified in the range of -1.5 or more and -0.5 or less. Although the C bal value indicates − (minus), this is a theoretical value, and even if C bal is within this range, C remains in the matrix in an actual alloy.
When Cbal is less than -1.5, martensite formation is reduced, and the hardness required for the alloy cannot be obtained. On the other hand, if C bal is larger than −0.5, the martensite is excessively advanced and the hardness becomes high, and the toughness suitable for the purpose of the present invention cannot be obtained.
C stic is given by the following equation according to the type of carbide forming element.
C stic = 0.06Cr + 0.063Mo + 0.033W + 0.24V + 0.25Ti + 0.13Nb + 0.066Ta
The high-speed steel-based sintered alloy of the present invention includes C, Cr, Mo, W, V, Ti, Nb, and Ta so that Cbal is in the range of −1.5 or more and −0.5 or less. By adjusting the above, the quenching performance in the heat treatment was lowered. Thereby, even if it heat-processes on the same conditions as general high speed steel, the hardness obtained is a comparatively low range (HRC50-62), and high toughness can be acquired.
本発明の高速度系焼結合金は、上記成分を含有し、残部Ｆｅ及び不可避の不純物からなるが、所望により、Ｎｉ、Ｎ及びＣｏをさらに含有させることもできる。 The high-speed sintered alloy of the present invention contains the above components and consists of the balance Fe and unavoidable impurities, but may further contain Ni, N, and Co if desired.
Ｎｉ：０.５〜３％
Ｎｉはオーステナイト相安定化元素であり、残留オーステナイト量の増加により靱性の向上に寄与する。また、耐食性を改善する元素でもある。このため、少なくとも０.５％以上含有させることが好ましい。一方、含有量が３％を越えると焼入れ性を著しく低下させるため、上限は３％に規定する。
Ni: 0.5 to 3%
Ni is an austenite phase stabilizing element and contributes to the improvement of toughness by increasing the amount of retained austenite. It is also an element that improves corrosion resistance. For this reason, it is preferable to contain at least 0.5% or more. On the other hand, if the content exceeds 3%, the hardenability is remarkably lowered, so the upper limit is defined as 3%.
Ｎ：０.１〜０.５％
Ｎは、Ｎｉと同様、オーステナイト相安定化元素であり、残留オーステナイト量の増加により靱性の向上に寄与すると共に耐食性を改善する。このため、少なくとも０.１％以上含有させることが好ましい。一方、含有量が０.５％を越えると焼入れ性を著しく低下を招くため、上限は０.５％に規定する。
なお、ＮはＮｉの約５倍の含有効果を有する。このため、ＮとＮｉを両方含有する場合は、Ｎｉ＋５Ｎを、０.５〜３％の範囲で含有することが好ましい。
N: 0.1-0.5%
N, like Ni, is an austenite phase stabilizing element and contributes to the improvement of toughness by increasing the amount of retained austenite and also improves the corrosion resistance. For this reason, it is preferable to contain at least 0.1% or more. On the other hand, if the content exceeds 0.5%, the hardenability is remarkably reduced, so the upper limit is specified to 0.5%.
N has a content effect about five times that of Ni. For this reason, when both N and Ni are contained, it is preferable to contain Ni + 5N in the range of 0.5 to 3%.
Ｃｏ：７〜２０％
Ｃｏはマトリックスに固溶してマトリックスを強化し、高温における耐力を著しく向上させる。このため、高温に曝される部材の材料にはＣｏを少なくとも７％以上含有させることが好ましく、８％以上含有させることがより好ましい。一方、あまりに多く含有すると靱性の低下を招く。このため、上限は２０％とするが、１２％以下がより好ましい。
Co: 7-20%
Co dissolves in the matrix and strengthens the matrix, significantly improving the yield strength at high temperatures. For this reason, it is preferable to contain at least 7% or more Co in the material of the member exposed to high temperature, and it is more preferable to contain 8% or more. On the other hand, when it contains too much, the toughness will be reduced. For this reason, although an upper limit is 20%, 12% or less is more preferable.
次に本発明の具体的実施例を掲げる。
表１に示す合金成分(重量％)の高速度鋼系合金粉末(粒径約３００μｍ以下)を原料粉末として使用し、ＨＩＰ処理を施して丸棒状の焼結合金(外径５０ｍｍ×長さ１５０ｍｍ)を得た。ＨＩＰ処理条件は、温度：１１５０℃、加圧力：１０００気圧、保持時間：３時間である。但し、No.１０４は、鋳造により調製した合金である。
次にこれら合金に焼入れ焼戻し熱処理を施して供試材を作製した。焼入れは、真空焼入れ炉にて１２００℃に１時間保持後、常温常圧の窒素ガスを導入し、ガス冷却することにより行なった。焼戻しは、５４０℃に５時間保持した後放冷するヒートパターンを３回繰り返した。
Next, specific examples of the present invention will be given.
A high-speed steel alloy powder (particle size of about 300 μm or less) of the alloy components (% by weight) shown in Table 1 is used as a raw material powder, and subjected to HIP treatment to form a round bar-like sintered alloy (outer diameter 50 mm × length 150 mm) ) The HIP treatment conditions are as follows: temperature: 1150 ° C., applied pressure: 1000 atm, and holding time: 3 hours. However, No. 104 is an alloy prepared by casting.
Next, these alloys were subjected to quenching and tempering heat treatments to prepare test materials. Quenching was performed by holding nitrogen gas at normal temperature and pressure after holding at 1200 ° C. for 1 hour in a vacuum quenching furnace and cooling the gas. For tempering, a heat pattern of holding for 5 hours at 540 ° C. and then allowing to cool was repeated three times.
各供試材について、硬度測定、摩耗試験及びシャルピー衝撃試験を行なった。
硬度はロックウエル硬度計のＣスケールで測定した。
摩耗試験は、大越式摩耗試験機を使用し、比摩耗量(１０-14ｍｍ2／Ｎ)を測定した。試験条件は、回転輪材質：ＳＵＪ２(ＨＲＣ６０)、摩耗速度：３.３８ｍ／ｓ、摩耗距離：４００ｍ、最終荷重６０Ｎにて行なった。
シャルピー衝撃試験は、５ｍｍ×５ｍｍ×５５ｍｍ、ノッチ無しの試験片を用い、常温で実施した。吸収エネルギー(Ｊ)を断面積(ｍ2)で除した値(Ｊ／ｍ2)を比較した。
試験結果を表１に示す。
Each specimen was subjected to hardness measurement, wear test and Charpy impact test.
The hardness was measured with a C scale of a Rockwell hardness tester.
In the abrasion test, a specific abrasion amount (10 −14 mm 2 / N) was measured using an Ogoshi type abrasion tester. The test conditions were as follows: rotating wheel material: SUJ2 (HRC60), wear rate: 3.38 m / s, wear distance: 400 m, and final load 60 N.
The Charpy impact test was performed at room temperature using a 5 mm × 5 mm × 55 mm, non-notched test piece. Absorbing energy (J) was compared by dividing the value (J / m 2) by the cross-sectional area (m 2).
The test results are shown in Table 1.
表１を参照すると、No.１〜No.１９は本発明の実施例であり、No.１０１〜No.１０９は比較例である。
発明例中、No.１〜No.３は、ＮｉとＮを両方とも含まない例であり、No.４〜No.１９は、Ｎｉ及びＮのうちの少なくとも一種を含む例である。これら発明例は、比較例No.１０１〜No.１０９と比べて、耐摩耗性(硬度及び比摩耗量)及び靱性(シャルピー衝撃値)について効果的な組合せを有することがわかる。
Referring to Table 1, No. 1 to No. 19 are examples of the present invention, and No. 101 to No. 109 are comparative examples.
In the inventive examples, No. 1 to No. 3 are examples that do not include both Ni and N, and No. 4 to No. 19 are examples that include at least one of Ni and N. It can be seen that these inventive examples have an effective combination of wear resistance (hardness and specific wear) and toughness (Charpy impact value) as compared with Comparative Examples No. 101 to No. 109.
発明例の中で、Ｃbalの値が同じ−０.６４であるNo.４、No.６及びNo.７と、Ｎｉ及びＮを両方とも含まないNo.２とを比較すると、前者は後者よりも衝撃値が向上していることが認められる。これは、Ｎｉ、Ｎの含有によりオーステナイトが安定化して残留オーステナイト量が増加し、高硬度化が抑えられたためと考えられる。 Among the invention examples, No.4 value of C bal is the same -0.64, the No.6 and No.7, is compared with the No.2 free both of the Ni and N, the former to the latter It is recognized that the impact value is improved. This is presumably because the austenite was stabilized by the inclusion of Ni and N, the amount of retained austenite increased, and the increase in hardness was suppressed.
比較例中、No.１０１及びNo.１０２は、Ｃの含有量が本発明の上限を越えており、耐摩耗性は良好であるが、靱性が著しく劣っている。
No.１０３は、Ｎｉの含有量が本発明の上限を越える例であり、Ｃbalの値は本発明の範囲内にあるが、十分な硬度が得られず、耐摩耗性に劣る。焼入れ性が低下したためである。
No.１０４〜No.１０９は、Ｃbalの値が本発明の範囲から逸脱する例である。
No.１０４、No.１０５及びNo.１０８は、ＮｉとＮを両方含まず、Ｃbalの値が本発明の範囲よりも大きい例である。ＮｉとＮを含まない発明例(No.１〜No.３)と比較すると、耐摩耗性はすぐれるが衝撃値が著しく劣る。なお、Ｎｉ、Ｎを含む比較例No.１０６及びNo.１０７についても、同様な結果を示している。これらの比較例は、熱処理時のマルテンサイト変態量が多すぎるためである。
No.１０９は、ＮｉとＮを両方含まず、Ｃbalの値が本発明の範囲よりも小さい例である。マトリックスに残存するＣがあまりにも少ないため、十分な硬度が得られず、所定の耐摩耗性を確保することができない。
In the comparative examples, No. 101 and No. 102 have the C content exceeding the upper limit of the present invention, and the wear resistance is good, but the toughness is remarkably inferior.
No. 103 is an example in which the Ni content exceeds the upper limit of the present invention, and the value of C bal is within the range of the present invention, but sufficient hardness cannot be obtained and the wear resistance is inferior. This is because the hardenability has decreased.
No.104~No.109 the value of C bal are examples departing from the scope of the present invention.
No. 104, No. 105 and No. 108 are examples in which both Ni and N are not included and the value of Cbal is larger than the range of the present invention. Compared with the invention examples containing no Ni and N (No. 1 to No. 3), the wear resistance is excellent, but the impact value is remarkably inferior. Similar results are shown for Comparative Examples No. 106 and No. 107 containing Ni and N. These comparative examples are because the amount of martensitic transformation during heat treatment is too large.
No. 109 is an example in which both Ni and N are not included and the value of C bal is smaller than the range of the present invention. Since there is too little C remaining in the matrix, sufficient hardness cannot be obtained, and predetermined wear resistance cannot be ensured.
本発明の焼結合金を用いた部材は、耐摩耗性及び耐事故性にすぐれるから、これらの特性が重要な鋼材の熱間圧延又は冷間圧延用ロール、塑性加工用金型、プラスチック成形機のシリンダー、スクリュー等の材料として有用である。 Since the member using the sintered alloy of the present invention is excellent in wear resistance and accident resistance, a roll for hot rolling or cold rolling of steel materials in which these characteristics are important, a mold for plastic working, plastic molding It is useful as a material for machine cylinders and screws.
Claims (4)
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| JP2015127455A (en) * | 2013-11-27 | 2015-07-09 | 山陽特殊製鋼株式会社 | Powder high speed tool steel |
| JP2016211022A (en) * | 2015-04-30 | 2016-12-15 | 山陽特殊製鋼株式会社 | Nitrided powder high speed tool steel excellent in hardness, toughness and wear resistance |
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